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US20190323100A1 - Method for producing grain-oriented electrical steel sheet - Google Patents

Method for producing grain-oriented electrical steel sheet Download PDF

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Publication number
US20190323100A1
US20190323100A1 US16/344,441 US201716344441A US2019323100A1 US 20190323100 A1 US20190323100 A1 US 20190323100A1 US 201716344441 A US201716344441 A US 201716344441A US 2019323100 A1 US2019323100 A1 US 2019323100A1
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less
amount
heating
steel sheet
slab
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Inventor
Takeshi Imamura
Yuiko EHASHI
Masanori Takenaka
Hiroi Yamaguchi
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JFE Steel Corp
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JFE Steel Corp
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Assigned to JFE STEEL CORPORATION reassignment JFE STEEL CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: EHASHI, YUIKO, IMAMURA, TAKESHI, TAKENAKA, MASANORI, YAMAGUCHI, HIROI
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab
    • C—CHEMISTRY; METALLURGY
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/1211—Rapid solidification; Thin strip casting
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1222—Hot rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1233—Cold rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1266—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest between cold rolling steps
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1272—Final recrystallisation annealing
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    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
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    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14791—Fe-Si-Al based alloys, e.g. Sendust
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
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    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
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    • C22C2202/02—Magnetic
    • H—ELECTRICITY
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    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
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    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
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    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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    • Y02P10/20—Recycling

Definitions

  • the present disclosure relates to a method for producing a grain-oriented electrical steel sheet suitable for an iron core material of a transformer.
  • inhibitors secondary recrystallization of grains having Goss orientation during a purification annealing by using precipitates called inhibitors.
  • Using inhibitors is useful in stably developing secondary recrystallized grains but has required to perform a slab heating at high temperature of 1300° C. or more to once dissolve inhibitor forming components in order to disperse the inhibitors finely into steel. Since the inhibitors cause degradation of magnetic properties after the secondary recrystallization, removing the precipitates and inclusions such as the inhibitors from a steel substrate, by performing the purification annealing at a high temperature of 1100° C. or more and by controlling an atmosphere, has also been required.
  • JP 2002-212639 A proposes a method to utilize inhibitors which contain only a small amount of MnS and MnSe by removing Al as much as possible.
  • JP 2000-129356 A proposes a technique for developing Goss-oriented crystal grains by the secondary recrystallization without containing the inhibitor forming components.
  • This is a technique for secondary recrystallizing the grains having Goss orientation without using the inhibitors by eliminating impurities such as the inhibitor forming components as much as possible to reveal dependency of grain boundary energy of crystals at a time of primary recrystallization on misorientation angles at grain boundaries. And an effect thereof is referred to as a texture inhibition effect.
  • the technique for producing the grain-oriented electrical steel sheets without using the inhibitor forming components is expected to be compatible with the production technique using the thin slabs with an aim to cost reduction.
  • a problem of degradation in magnetic properties became newly apparent when producing the grain-oriented electrical steel sheets in combination with these production techniques.
  • a thin slab with a thickness of 64 mm was produced by a continuous casting process with using a molten steel containing, in mass %, C: 0.012%, Si: 3.30%, Mn: 0.050%, Al: 0.0027%, N: 0.0010%, S: 0.0009% and Se: 0.0010%.
  • a slab heating was performed prior to a hot rolling by passing the slab through a tunnel furnace on the way of conveying the slab to the step of hot rolling. The slab was heated with both of the heating temperature and the heating time variously changed in the heating process.
  • the hot rolling was started in about 35 seconds after completion of the slab heating process.
  • the thin slab was hot rolled to form a hot-rolled steel sheet with a thickness of 2.2 mm.
  • the hot-rolled steel sheet was subjected to a hot band annealing at 1000° C. for 30 seconds, followed by a cold rolling finishing into a sheet thickness of 0.27 mm.
  • a primary recrystallization annealing which also serves as a decarburization, was performed under soaking conditions of at 850° C.
  • Magnetic flux density B 8 of the obtained sample was measured according to the method described in JIS C 2550.
  • the result of the obtained magnetic flux density B 8 organized in relation to the heating temperature and the heating time in the heating process prior to the hot rolling is illustrated in FIG. 1 . It can be observed from FIG. 1 that the magnetic flux density is increased by controlling the temperature in the heating process to 1000° C. or more and 1300° C. or less, and the time in the heating process to 10 seconds or more and 600 seconds or less.
  • the thin slabs include slab structure comprising largely columnar crystals. This is thought to be due to equiaxial crystals being unlikely to be generated from a center part of the sheet thickness as the thin slabs, compared with thick slabs, cool faster when casted and have a larger temperature gradient at interfaces of solidified shells.
  • the slab structure of the columnar crystals, after the hot rolling, is known to generate hot rolling processed structure which is unlikely to recrystallize even in subsequent heat treatments.
  • This structure which is unlikely to recrystallize, affects the degradation of magnetic property in the grain-oriented electrical steel sheets after a final annealing. That is, it is presumed that the columnar crystals becoming main structure of the slab structure in the state prior to the hot rolling cause the magnetic degradation.
  • the columnar crystals need to be reduced in order for solving this problem. It is possible to reduce the columnar crystals in general steel products other than the electrical steel sheets as the general steel products involve ⁇ - ⁇ transformation so that the recrystallization occurs with the transformation in a temperature range of ⁇ -phase even in the columnar crystals formed in a high temperature range of ⁇ -phase.
  • the grain-oriented electrical steel sheets may have a single-phase structure in some cases as the grain-oriented electrical steel sheets prevent the ⁇ -transformation after the secondary recrystallization from destroying Goss-oriented grain-size microstructure, resulting in significantly low proportion of the ⁇ -phase. Because of this, it is difficult to reduce the columnar crystals in virtue of the aforementioned recrystallization with transformation in the temperature range of ⁇ -phase.
  • the heating temperature is excessively high for example when the heating temperature in the heating process is over 1300° C. or in a circumstance where the heating time is excessively long for example when the heating time is over 600 seconds, it is believed that the magnetic property of the product sheets degraded due to excessively coarse crystal grains generated instead of the columnar crystals and subsequent generation of the hot rolling processed structure being not easily recrystallized even with the heat treatments, similarly to the columnar crystals.
  • Newly adding and installing an apparatus having function of enhancing equiaxial crystals of the structure to existing production lines may be also considered as a solution to the problems related to the columnar crystals in the thin slabs.
  • the present disclosure is a new technique that can merge well the features of the structure of grain-oriented electrical steel sheets and the features of the continuous casting process with thin slabs, as well as that can minimize cost increase such from the installation of new apparatuses.
  • a method for producing a grain-oriented electrical steel sheet comprising:
  • molten steel subjecting a molten steel to continuous casting to form a slab with a thickness of 25 mm or more and 100 mm or less, the molten steel having a chemical composition containing (consisting of), in mass %,
  • step of heating the slab is performed at a temperature of 1000° C. or more and 1300° C. or less for a time of 10 seconds or more and 600 seconds or less.
  • the chemical composition further contains, in mass %, one or more selected from the group consisting of
  • Cu in an amount of 0.01% or more and 0.50% or less
  • Ni in an amount of 0.001% or more and 0.50% or less
  • Bi in an amount of 0.005% or more and 0.50% or less
  • Nb in an amount of 0.0010% or more and 0.0100% or less
  • V in an amount of 0.0010% or more and 0.0100% or less.
  • FIG. 1 is a graph illustrating a relationship between the heating temperature and the heating time in the heating process and the magnetic flux density B 8 .
  • a grain-oriented electrical steel sheet and a method for producing thereof according to one of the disclosed embodiments are described below. Firstly, reasons for limiting chemical composition of steel are described. In the description, “%” representing content (amount) of each component element denotes “mass %” unless otherwise noted.
  • the amount of C is limited to 0.100% or less. This is because, if the content of C exceeds 0.100%, it would be difficult to reduce the content to 0.005% or less where no magnetic aging occurs after a decarburization annealing. Meanwhile, if the content of C is less than 0.002%, an effect of grain boundary strengthening by C would be lost to cause defects, such as cracks occurred in slabs, that impede operability. Therefore, the amount of C should be 0.002% or more and 0.100% or less.
  • the amount of C is preferably 0.010% or more. And the amount of C is preferably 0.050% or less.
  • Si 2.00% or more and 8.00% or less
  • Si is an element necessary for increasing specific resistance of steel and improving iron loss properties.
  • the content of Si of 2.00% or more is required. Meanwhile, if the content of Si exceeds 8.00%, workability of steel degrades to make the rolling difficult. Therefore, the amount of Si should be 2.00% or more and 8.00% or less.
  • the amount of Si is preferably 2.50% or more. And the amount of Si is preferably 4.50% or less.
  • Mn 0.005% or more and 1.000% or less
  • Mn is an element necessary for providing favorable hot workability. For that purpose, the content of Mn of 0.005% or more is required. Meanwhile, if the content of Mn exceeds 1.000%, magnetic flux density of product sheets decreases. Therefore, the amount of Mn should be 0.005% or more and 1.000% or less.
  • the amount of Mn is preferably 0.040% or more. And the amount of Mn is preferably 0.200% or less.
  • each amount should be limited to Al: less than 0.0100%, N: less than 0.0050%, S: less than 0.0050% and Se: less than 0.0050%.
  • the amount of Al is preferably less than 0.0080%.
  • the amount of N is preferably less than 0.0040%.
  • the amount of S is preferably less than 0.0030%.
  • the amount of Se is preferably less than 0.0030%.
  • the present disclosure can appropriately contain one or more selected from among, Cr in an amount of 0.01% or more, Cr in an amount of 0.50% or less, Cu in an amount of 0.01% or more, Cu in an amount of 0.50% or less, P in an amount of 0.005% or more, P in an amount of 0.50% or less, Ni in an amount of 0.001% or more, Ni in an amount of 0.50% or less, Sb in an amount of 0.005% or more, Sb in an amount of 0.50% or less, Sn in an amount of 0.005% or more, Sn in an amount of 0.50% or less, Bi in an amount of 0.005% or more, Bi in an amount of 0.50% or less, Mo in an amount of 0.005% or more, Mo in an amount of 0.100% or less, B in an amount of 0.0002% or more, B in an amount of 0.0025% or less, Nb in an amount of 0.0010% or more, Nb in an amount of 0.0100% or less, V in an amount of Cr in an amount of 0.0
  • a slab is produced through a continuous casting process from a molten steel having the aforementioned chemical composition. Thickness of the produced slab is designed to be 100 mm or less in order for cost reduction. Meanwhile, the thickness of the slab is designed to be 25 mm or more. This is because the thinner the thickness of the slab is, the faster solidification reaches to a center of the slab when cooled, leaving the slab more difficult to be adjusted afterward.
  • the thickness of the slab is preferably 40 mm or more. And the thickness of the slab is preferably 80 mm or less.
  • heating temperature 1000° C. or more and 1300° C. or less, as well as heating time of 10 seconds or more and 600 seconds or less, are essential as heating conditions.
  • the heating temperature is preferably 1250° C. or less, and the heating time is preferably 300 seconds or less, both from the viewpoint of cost reduction. Further, the heating temperature is preferably 1110° C. or more, and the heating temperature is preferably 1200° C. or less, both from the viewpoint of the magnetic property. And the heating time is preferably 10 seconds or more, and the heating time is preferably 200 seconds or less, both from the viewpoint of the magnetic property as well. In addition, at least a part of the heating may be performed by an induction heating in the heating process.
  • the induction heating is a method to heat with self-heating, for example, by applying an alternating magnetic field to a slab.
  • the heating method it is preferable to maintain heated during conveyance with using an apparatus, in which a conveyance table and a heating furnace are integrated, called a tunnel furnace. Fluctuation of the temperature within the slab can be suppressed by this method.
  • the heating furnace has a skid and the slab is conveyed in a direction of the slab width with the slab being lifted intermittently by a walking beam and so forth during the heating.
  • a problem arises that the slab droops due to its thinness upon lifted in the furnace.
  • considerable drop in temperature at a skid part directly affects the magnetic degradation at a corresponding part of a product sheet. Therefore, the above method is inappropriate when using the thin slabs.
  • a method of heating while conveying the slab in parallel to a casting direction of the slab such as a tunnel furnace method, is desirable in the present disclosure.
  • a hot rolling is performed after the aforementioned heating. Given that the slab is thin, it is desirable to omit a rough rolling and only perform a finish rolling through a tandem mill from the viewpoint of cost.
  • a start temperature of 900° C. or more as well as a finish temperature of 700° C. or more are desirable, both for obtaining favorable final magnetic property in the inhibitor-less chemical component.
  • the finish temperature is desirably 1000° C. or less as a shape after the rolling tends to be unfavorable when the finish temperature is too high.
  • a hot band annealing is performed as needed to a hot-rolled steel sheet obtained through the hot rolling.
  • temperature of the hot band annealing is preferably 800° C. or more, and the temperature of the hot band annealing is preferably 1150° C. or less.
  • the temperature of the hot band annealing is less than 800° C., band texture from the hot rolling remains to make it difficult to achieve a primary recrystallized microstructure with uniformly-sized grains, resulting in impeding development of a secondary recrystallization.
  • the temperature of the hot band annealing is desirably 950° C. or more. And the temperature of the hot band annealing is desirably 1080° C. or less.
  • Annealing time is preferably 10 seconds or more. And the annealing time is preferably 200 seconds or less. The band texture tends to remain when the annealing time is less than 10 seconds.
  • the annealing time exceeds 200 seconds, a concern arises that segregate-able elements and so forth segregate to grain boundaries so that defects such as cracks and the like may occur easily during a subsequent cold rolling.
  • a cold rolling is performed once or more with an intermediate annealing(s) in between, as needed, to form a cold-rolled steel sheet having a final sheet thickness.
  • Temperature of the intermediate annealing is preferably 900° C. or more.
  • the temperature of the intermediate annealing is preferably 1200° C. or less.
  • the temperature of the intermediate annealing is less than 900° C., the recrystallized grains become finer and the primary recrystallized microstructure has less Goss nuclei, resulting in the magnetic degradation.
  • the temperature of the intermediate annealing exceeds 1200° C., the grain size grows too coarse to make it extremely disadvantageous for achieving the primary recrystallized microstructure with uniformly-sized grains, as with the hot band annealing.
  • the temperature of the intermediate annealing is more preferably in an approximate range from 900° C. to 1150° C.
  • performing the cold rolling with an increased temperature to 100° C. to 300° C. is effective, and performing an aging treatment once or more within a temperature range from 100° C. to 300° C. during the cold rolling is also effective, both in order for improving the magnetic property by changing recrystallized texture.
  • a primary recrystallization annealing is performed after the aforementioned cold rolling.
  • the primary recrystallization annealing may also serve as a decarburization annealing.
  • An annealing temperature of 800° C. or more is effective, and the annealing temperature of 900° C. or less is also effective, both from the viewpoint of decarburization.
  • An atmosphere is desirably wet from the viewpoint of decarburization.
  • annealing time is preferably in an approximate range from 30 seconds to 300 seconds. However, these will not apply to a case with C contained only in an amount of 0.005% or less where the decarburization is unnecessary.
  • An annealing separator is applied, as needed, to a steel sheet after the aforementioned primary recrystallization annealing.
  • the forsterite film is formed while a secondary recrystallized microstructure is developed by applying the annealing separator mainly containing MgO followed by performing a secondary recrystallization annealing which also serves as a purification annealing.
  • the annealing separator will not be applied, or even if applied, silica, alumina and so forth are used instead of MgO as MgO forms the forsterite film.
  • an electrostatic coating and the like which does not introduce water is effective. Heat resistant inorganic material sheets, for example, silica, alumina and mica, may also be used.
  • a secondary recrystallization annealing is performed after the aforementioned primary recrystallization annealing or applying the annealing separator.
  • the secondary recrystallization annealing may also serve as a purification annealing.
  • the secondary recrystallization annealing, serving as the purification annealing as well, is desirably performed at a temperature of 800° C. or more in order to generate a secondary recrystallization. Further, it is desirable to retain the temperature at 800° C. or more for 20 hours or more in order to complete the secondary recrystallization.
  • a flattening annealing may further be performed after the aforementioned secondary recrystallization annealing.
  • adhered annealing separator will be removed by water washing, brushing and/or acid cleaning in a circumstance where the annealing separator was applied. It is effective to subsequently adjust shape by performing the flattening annealing in order to reduce iron loss.
  • Preferable temperature of the flattening annealing is in an approximate range from 700° C. to 900° C. from the viewpoint of shape adjustment.
  • Coatings that can impart tension to the steel sheets are desirable for reducing the iron loss. It is preferable to adopt coating methods such as a tension coating via a binder, as well as a physical vapor deposition and a chemical vapor deposition to deposit inorganic substances onto the surface layer of steel sheets. This is because these methods are excellent in a coating adhesion property and allow to obtain an effect of considerable reduction of the iron loss.
  • a magnetic domain refining treatment can be performed after the aforementioned flattening annealing in order to reduce iron loss.
  • the treatment methods include, for example, methods that are commonly practiced such as grooving a steel sheet after final annealing; introducing a linear thermal strain or impact strain by laser or electron beam; and grooving beforehand an intermediate product such as a cold-rolled sheet with a final sheet thickness.
  • the other production conditions may be according to those for general grain-oriented electrical steel sheets.
  • a slab having a thickness of 60 mm was produced by continuous casting from a molten steel containing, in mass %, C: 0.015%, Si: 3.25%, Mn: 0.040%, Al: 0.0020%, N: 0.0009% and S: 0.0012%, with the balance being Fe and inevitable impurities.
  • a heating treatment was performed in a tunnel furnace of regenerative burner heating type under the conditions described in Table 1. After 45 seconds of this, a hot rolling was performed to finish to a thickness of 2.2 mm. A hot band annealing was then performed at a temperature of 975° C. for 30 seconds, followed by a cold rolling to finish to a sheet thickness of 0.23 mm.
  • a primary recrystallization annealing which also serves as a decarburization annealing, was performed under soaking conditions of at 840° C. for 60 seconds in an atmosphere of 50% H 2 +50% N 2 with a dew point of 55° C., followed by applying an annealing separator mainly containing MgO.
  • a secondary recrystallization annealing which also serves as a purification annealing, was performed with retaining a temperature at 1200° C. for 10 hours in a H 2 atmosphere.
  • a flattening annealing which also serves as formation of a tension imparting coating mainly containing magnesium phosphate and chromic acid, was performed under conditions of at 820° C. for 15 seconds.
  • Magnetic flux density B 8 of thus obtained sample was measured according to a method described in JIS C 2550 and the result thereof is also described in Table 1. As is apparent from Table 1, the steel sheets obtained according to the present disclosure have favorable magnetic properties.
  • a slab having a thickness of 45 mm was produced by continuous casting from a molten steel containing the chemical composition described in Table 2 with the balance being Fe and inevitable impurities.
  • the slab was passed through a tunnel furnace in which a temperature is retained at 1200° C., and the temperature was continuously retained at 1200° C. for 150 seconds. After 65 seconds from this, a hot rolling was performed to finish to a thickness of 3.0 mm.
  • a slab conveyance rate during the heating process in the tunnel furnace was set to 25 m/min.
  • heating up to a temperature of 700° C. was performed by an induction heating, while the further heating and heat retention was performed by a gas burner.
  • a hot band annealing was then performed at a temperature of 1000° C. for 60 seconds, followed by a cold rolling to a sheet thickness of 0.9 mm.
  • an intermediate annealing was performed at a temperature of 1000° C. for 100 seconds, followed by a cold rolling to finish to a thickness of 0.23 mm.
  • a primary recrystallization annealing which also serves as a decarburization annealing, was performed under soaking conditions of at 820° C. for 20 seconds in an atmosphere of 50% H 2 +50% N 2 with a dew point of 55° C., followed by applying an annealing separator mainly containing MgO.
  • a secondary recrystallization annealing which also serves as a purification annealing, was performed with retaining a temperature at 1150° C. for 3 hours in a H 2 atmosphere.
  • a flattening annealing which also serves as formation of a tension imparting coating mainly containing magnesium phosphate and chromic acid, was performed under conditions of at 850° C. for 10 seconds.
  • Magnetic flux density B 8 of thus obtained sample was measured according to a method described in JIS C 2550 and the result thereof is also described in Table 2. As is apparent from Table 2, the steel sheets obtained according to the present disclosure have favorable magnetic properties.
  • the present disclosure does not only allow to stably obtain excellent magnetic properties in grain-oriented electrical steel sheets produced from thin slabs without using inhibitor forming components, but is also applicable to stainless steels having a single-phase structure same as that of the grain-oriented electrical steel sheets.

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US20220090226A1 (en) * 2019-01-16 2022-03-24 Nippon Steel Corporation Method for producing grain-oriented electrical steel sheet
US11286538B2 (en) * 2017-02-20 2022-03-29 Jfe Steel Corporation Method for manufacturing grain-oriented electrical steel sheet
US20220098691A1 (en) * 2019-01-16 2022-03-31 Nippon Steel Corporation Method for manufacturing grain-oriented electrical steel sheet
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US11286538B2 (en) * 2017-02-20 2022-03-29 Jfe Steel Corporation Method for manufacturing grain-oriented electrical steel sheet
US20220090226A1 (en) * 2019-01-16 2022-03-24 Nippon Steel Corporation Method for producing grain-oriented electrical steel sheet
US20220098691A1 (en) * 2019-01-16 2022-03-31 Nippon Steel Corporation Method for manufacturing grain-oriented electrical steel sheet
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